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WO2019163661A1 - Alliage magnétique doux et composant magnétique - Google Patents

Alliage magnétique doux et composant magnétique Download PDF

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Publication number
WO2019163661A1
WO2019163661A1 PCT/JP2019/005514 JP2019005514W WO2019163661A1 WO 2019163661 A1 WO2019163661 A1 WO 2019163661A1 JP 2019005514 W JP2019005514 W JP 2019005514W WO 2019163661 A1 WO2019163661 A1 WO 2019163661A1
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Prior art keywords
soft magnetic
magnetic alloy
alloy according
flux density
alloy
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PCT/JP2019/005514
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English (en)
Japanese (ja)
Inventor
一 天野
明洋 原田
和宏 吉留
賢治 堀野
裕之 松元
健輔 荒
暁斗 長谷川
誠吾 野老
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TDK Corp
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TDK Corp
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Priority to CN201980014084.5A priority Critical patent/CN111771010A/zh
Priority to US16/971,477 priority patent/US20200377982A1/en
Publication of WO2019163661A1 publication Critical patent/WO2019163661A1/fr
Anticipated expiration legal-status Critical
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
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    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/05—Metallic powder characterised by the size or surface area of the particles
    • B22F1/054—Nanosized particles
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/02—Amorphous alloys with iron as the major constituent
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15333—Amorphous metallic alloys, e.g. glassy metals containing nanocrystallites, e.g. obtained by annealing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • B22F1/142—Thermal or thermo-mechanical treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
    • B22F2009/0828—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid with water
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B22F2009/0844—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid in controlled atmosphere
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/35—Iron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/10—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying using centrifugal force
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2200/00—Crystalline structure
    • C22C2200/04—Nanocrystalline
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic

Definitions

  • the present invention relates to a soft magnetic alloy and a magnetic component.
  • Patent Document 1 describes an Fe-based soft magnetic alloy having a fine crystal grain size.
  • a nanocrystalline material can provide a higher saturation magnetic flux density or the like than a conventional crystalline material such as FeSi or an amorphous material such as FeSiB.
  • An object of the present invention is to provide a soft magnetic alloy having a high saturation magnetic flux density, a low coercive force, and a high specific resistance.
  • the soft magnetic alloy according to the present invention comprises: Composition formula (Fe (1- ( ⁇ + ⁇ )) X1 ⁇ X2 ⁇ ) a (1- (a + b + c + d + e)) M a Si b Cu c soft magnetic alloy consisting of X3 d B e,
  • X1 is one or more selected from the group consisting of Co and Ni
  • X2 is one or more selected from the group consisting of Ti, V, Mn, Ag, Zn, Al, Sn, As, Sb, Bi and rare earth elements
  • X3 is one or more selected from the group consisting of C and Ge
  • M is at least one selected from the group consisting of Zr, Nb, Hf, Ta, Mo and W; 0.030 ⁇ a ⁇ 0.120 0.020 ⁇ b ⁇ 0.175 0 ⁇ c ⁇ 0.020 0 ⁇ d ⁇ 0.100 0 ⁇ e ⁇ 0.030 ⁇ ⁇ ⁇
  • the soft magnetic alloy according to the present invention has the above-described characteristics, and thus tends to have a structure that is likely to become an Fe-based nanocrystalline alloy by heat treatment. Furthermore, the Fe-based nanocrystalline alloy having the above characteristics has a preferable soft magnetic characteristic of a high saturation magnetic flux density and a low coercive force, and further becomes a soft magnetic alloy having a high specific resistance.
  • the soft magnetic alloy according to the present invention may satisfy 0 ⁇ e ⁇ 0.010.
  • the soft magnetic alloy according to the present invention may satisfy 0 ⁇ e ⁇ 0.001.
  • the soft magnetic alloy according to the present invention may satisfy 0.730 ⁇ 1- (a + b + c + d + e) ⁇ 0.930.
  • the soft magnetic alloy according to the present invention may satisfy 0 ⁇ ⁇ ⁇ 1 ⁇ (a + b + c + d + e) ⁇ ⁇ 0.40.
  • the soft magnetic alloy according to the present invention may satisfy 0 ⁇ ⁇ ⁇ 1- (a + b + c + d + e) ⁇ ⁇ 0.030.
  • the soft magnetic alloy according to the present invention may have a nanoheterostructure in which initial microcrystals exist in an amorphous state.
  • the average grain size of the initial microcrystal may be 0.3 to 10 nm.
  • the soft magnetic alloy according to the present invention may have a structure made of Fe-based nanocrystals.
  • the average particle diameter of the Fe-based nanocrystal may be 5 to 30 nm.
  • the soft magnetic alloy according to the present invention may have a ribbon shape.
  • the soft magnetic alloy according to the present invention may be in a powder form.
  • the magnetic component according to the present invention is made of the above soft magnetic alloy.
  • Soft magnetic alloy according to the present embodiment, the composition formula (Fe (1- ( ⁇ + ⁇ )) X1 ⁇ X2 ⁇ ) there with (1- (a + b + c + d + e)) M a Si b Cu c X3 d soft magnetic alloy consisting of B e
  • X1 is one or more selected from the group consisting of Co and Ni
  • X2 is one or more selected from the group consisting of Ti, V, Mn, Ag, Zn, Al, Sn, As, Sb, Bi and rare earth elements
  • X3 is one or more selected from the group consisting of C and Ge
  • M is at least one selected from the group consisting of Zr, Nb, Hf, Ta, Mo and W; 0.030 ⁇ a ⁇ 0.120 0.020 ⁇ b ⁇ 0.175 0 ⁇ c ⁇ 0.020 0 ⁇ d ⁇ 0.100 0 ⁇ e ⁇ 0.030 ⁇ ⁇ 0 ⁇ 0
  • the soft magnetic alloy having the above composition is easily made into a soft magnetic alloy that is amorphous and does not include a crystal phase that is composed of crystals having a particle size larger than 15 nm. And when heat-treating the soft magnetic alloy, Fe-based nanocrystals are likely to precipitate. And the soft magnetic alloy containing Fe-based nanocrystal tends to have a high saturation magnetic flux density, a low coercive force, and a high specific resistance. Furthermore, the oxidation resistance tends to be high.
  • the soft magnetic alloy having the above composition is easily used as a starting material for the soft magnetic alloy in which Fe-based nanocrystals are precipitated.
  • the soft magnetic alloy before the heat treatment may be made entirely of amorphous material, but is composed of amorphous material and initial microcrystals having a particle size of 15 nm or less, and the initial microcrystals are in the amorphous state. It preferably has a nanoheterostructure present in When the initial microcrystal has a nanoheterostructure existing in an amorphous state, Fe-based nanocrystals are easily precipitated during heat treatment.
  • the initial crystallites preferably have an average particle size of 0.3 to 10 nm.
  • M content (a) satisfies 0.030 ⁇ a ⁇ 0.120.
  • the content (a) of M is preferably 0.050 ⁇ a ⁇ 0.100.
  • the Si content (b) satisfies 0.020 ⁇ b ⁇ 0.175.
  • the Si content (b) preferably satisfies 0.030 ⁇ b ⁇ 0.100.
  • Cu content (c) satisfies 0 ⁇ c ⁇ 0.020. That is, Cu does not have to be contained.
  • the saturation magnetic flux density increases as the Cu content decreases, and the coercive force tends to decrease as the Cu content increases.
  • c is too large, the saturation magnetic flux density is too low.
  • X3 is at least one selected from the group consisting of C and Ge.
  • the content (d) of X3 satisfies 0 ⁇ d ⁇ 0.100. That is, X3 may not be contained.
  • the content (d) of X3 is preferably 0 ⁇ d ⁇ 0.050. When the content of X3 is too large, the saturation magnetic flux density tends to be low, and the coercive force tends to be high.
  • B content (e) satisfies 0 ⁇ e ⁇ 0.030. That is, B may not be contained. Furthermore, it is preferable that 0 ⁇ e ⁇ 0.010, and it is further preferable that B is not substantially contained. Note that “substantially not containing B” refers to the case of 0 ⁇ e ⁇ 0.001. When the content of B is large, the saturation magnetic flux density tends to be low, and the coercive force is likely to be high.
  • the Fe content (1- (a + b + c + d + e)) is not particularly limited, but preferably satisfies 0.730 ⁇ 1- (a + b + c + d + e) ⁇ 0.930. 0.780 ⁇ 1 ⁇ (a + b + c + d + e) ⁇ 0.930 may be satisfied.
  • the saturation magnetic flux density is easily improved and the coercive force is easily reduced.
  • a part of Fe may be substituted with X1 and / or X2.
  • X1 is at least one selected from the group consisting of Co and Ni.
  • the number of atoms of X1 is preferably 40 at% or less, where the total number of atoms in the composition is 100 at%. That is, it is preferable to satisfy 0 ⁇ ⁇ ⁇ 1 ⁇ (a + b + c + d + e) ⁇ ⁇ 0.40.
  • the range of substitution amount for substituting Fe with X1 and / or X2 is 0 ⁇ ⁇ + ⁇ ⁇ 0.55. In the case of ⁇ + ⁇ > 0.55, it becomes difficult to form an Fe-based nanocrystalline alloy by heat treatment, and even if the Fe-based nanocrystalline alloy is formed, the coercive force tends to increase.
  • the soft magnetic alloy according to this embodiment may contain elements other than the above as inevitable impurities. Further, elements other than the above may be contained in total less than 1% by weight with respect to 100% by weight of the soft magnetic alloy.
  • the single roll method first, pure metals of each metal element contained in the finally obtained soft magnetic alloy are prepared and weighed so as to have the same composition as the finally obtained soft magnetic alloy. And the pure metal of each metal element is melt
  • the method for dissolving the pure metal is not particularly limited. For example, there is a method in which the pure metal is melted by high-frequency heating after evacuation in a chamber.
  • the master alloy and the soft magnetic alloy consisting of the finally obtained Fe-based nanocrystal usually have the same composition.
  • the thickness of the ribbon obtained mainly by adjusting the rotation speed of the roll can be adjusted, but for example, by adjusting the interval between the nozzle and the roll, the temperature of the molten metal, etc.
  • the thickness of the obtained ribbon can be adjusted.
  • the thickness of the ribbon is not particularly limited, but can be 5 to 30 ⁇ m, for example.
  • the ribbon is amorphous with no crystal having a particle size larger than 15 nm.
  • An Fe-based nanocrystalline alloy can be obtained by subjecting the amorphous ribbon to a heat treatment described later.
  • the thin ribbon before the heat treatment may not contain any initial crystallites having a particle size of less than 15 nm, but preferably contains initial crystallites. That is, it is preferable that the ribbon before the heat treatment has a nanoheterostructure composed of amorphous and the initial microcrystals present in the amorphous.
  • the particle size of the initial microcrystal is not particularly limited, but the average particle size is preferably in the range of 0.3 to 10 nm.
  • the roll temperature is preferably 4 to 30 ° C. to make it amorphous.
  • the higher the rotation speed of the roll the smaller the average grain size of the initial crystallites, and 30 to 40 m / sec. Is preferable in order to obtain initial microcrystals having an average particle size of 0.3 to 10 nm.
  • the atmosphere inside the chamber is preferably in the air considering cost.
  • the heat treatment conditions for producing the Fe-based nanocrystalline alloy there are no particular restrictions on the heat treatment conditions for producing the Fe-based nanocrystalline alloy.
  • Preferred heat treatment conditions vary depending on the composition of the soft magnetic alloy. Usually, the preferred heat treatment temperature is about 400 to 600 ° C., and the preferred heat treatment time is about 10 minutes to 10 hours. However, depending on the composition, there may be a preferred heat treatment temperature and heat treatment time outside the above range.
  • the method for calculating the average particle diameter in the obtained Fe-based nanocrystalline alloy can be calculated by observing using a transmission electron microscope.
  • the method for confirming that the crystal structure is bcc (body-centered cubic lattice structure).
  • it can be confirmed using X-ray diffraction measurement.
  • a molten alloy at 1200 to 1500 ° C. is obtained in the same manner as the single roll method described above. Thereafter, the molten alloy is sprayed in a chamber to produce a powder.
  • the preferable nanoheterostructure can be easily obtained.
  • thermodynamic equilibrium state can be reached in a short time, strain and stress can be removed, and an Fe-based soft magnetic alloy having an average particle size of 10 to 50 nm can be easily obtained.
  • the shape of the soft magnetic alloy according to this embodiment is not particularly limited. As described above, a ribbon shape and a powder shape are exemplified, but a block shape and the like are also conceivable.
  • the use of the soft magnetic alloy (Fe-based nanocrystalline alloy) according to the present embodiment is not particularly limited.
  • magnetic parts are mentioned, and among these, a magnetic core is particularly mentioned. It can be suitably used as a magnetic core for an inductor, particularly a power inductor.
  • the soft magnetic alloy according to this embodiment can be suitably used for a thin film inductor and a magnetic head in addition to a magnetic core.
  • a method for obtaining a magnetic component in particular, a magnetic core and an inductor from the soft magnetic alloy according to the present embodiment will be described.
  • a method for obtaining the magnetic core and the inductor from the soft magnetic alloy according to the present embodiment is not limited to the following method.
  • applications of magnetic cores include transformers and motors.
  • Examples of a method for obtaining a magnetic core from a ribbon-shaped soft magnetic alloy include a method of winding a ribbon-shaped soft magnetic alloy and a method of laminating. When laminating thin ribbon-shaped soft magnetic alloys via an insulator, a magnetic core with further improved characteristics can be obtained.
  • a method for obtaining a magnetic core from a soft magnetic alloy in the form of a powder for example, a method in which a magnetic core is appropriately mixed with a binder and then molded using a mold can be mentioned.
  • a method in which a magnetic core is appropriately mixed with a binder and then molded using a mold can be mentioned.
  • an oxidation treatment, an insulating film or the like to the powder surface before mixing with the binder, the specific resistance is improved and the magnetic core is adapted to a higher frequency band.
  • the molding method is not particularly limited, and examples thereof include molding using a mold and molding.
  • the space factor is 70% or more, 1.6%.
  • a magnetic core having a magnetic flux density of 0.45 T or more and a specific resistance of 1 ⁇ ⁇ cm or more when a magnetic field of ⁇ 10 4 A / m is applied can be obtained.
  • the above characteristics are equivalent to or better than general ferrite cores.
  • the space factor is 80%.
  • a dust core having a magnetic flux density of 0.9 T or more and a specific resistance of 0.1 ⁇ ⁇ cm or more when a magnetic field of 1.6 ⁇ 10 4 A / m is applied can be obtained.
  • the above characteristics are superior to general dust cores.
  • the molded body having the above-described magnetic core is subjected to heat treatment after molding as a strain relief heat treatment, thereby further reducing core loss and increasing usefulness. Note that the core loss of the magnetic core is reduced by reducing the coercive force of the magnetic body constituting the magnetic core.
  • an inductance component can be obtained by winding the magnetic core.
  • the manner in which the winding is applied and the method of manufacturing the inductance component For example, a method of winding a winding at least one turn or more around the magnetic core manufactured by the above method can be mentioned.
  • a soft magnetic alloy paste obtained by adding a binder and a solvent to the soft magnetic alloy particles and a paste obtained by adding a binder and a solvent to the conductor metal for the coil can be obtained by heating and firing after alternately laminating and laminating the conductive paste.
  • an inductance component in which the coil is built in the magnetic body is obtained. Can be obtained.
  • a soft magnetic alloy powder having a maximum particle size of 45 ⁇ m or less and a center particle size (D50) of 30 ⁇ m or less. It is preferable for obtaining the Q characteristic.
  • a sieve having an opening of 45 ⁇ m may be used, and only the soft magnetic alloy powder passing through the sieve may be used.
  • the Q value in the high frequency region tends to decrease as the soft magnetic alloy powder having a large maximum particle size is used. Particularly when the soft magnetic alloy powder having a maximum particle size exceeding 45 ⁇ m in the sieve diameter is used, The Q value may be greatly reduced. However, if the Q value in the high frequency region is not important, soft magnetic alloy powder having a large variation can be used. Since soft magnetic alloy powders with large variations can be manufactured at a relatively low cost, it is possible to reduce costs when using soft magnetic alloy powders with large variations.
  • the raw metal was weighed so as to have the alloy compositions of the examples and comparative examples shown in the table below, and was melted by high-frequency heating to prepare a master alloy.
  • the produced master alloy is heated and melted to form a molten metal at 1300 ° C., and then a 20 ° C. roll is rotated in the atmosphere at a rotational speed of 40 m / sec.
  • the metal was jetted onto a roll by the single roll method used in the above to create a ribbon.
  • the thickness of the ribbon was 20 to 25 ⁇ m, the width of the ribbon was about 15 mm, and the length of the ribbon was about 10 m.
  • the coercive force was 10.0 A / m or less, and 7.0 A / m or less was even better.
  • the specific resistance ( ⁇ ) is the specific resistance ( ⁇ ) of a ribbon (hereinafter also referred to as Fe 90 Zr 7 B 3 ribbon) prepared by the same manufacturing method as in Example 3 except that the composition is Fe 90 Zr 7 B 3. ) To 20% or more and less than 40%, the case where it rises is considered good, and the case where it rises 40% or more is considered even better.
  • Table 1 describes examples and comparative examples in which the content (a) of Zr was changed when M was only Zr and Cu, X3 and B were not included.
  • Comparative Example 1 in which the Zr content was too small, the ribbon before the heat treatment was composed of a crystalline phase, the coercive force Hc after the heat treatment was remarkably high, and the specific resistance ⁇ was low. Further, in Comparative Example 2 in which the Zr content was too large, the saturation magnetic flux density was lowered.
  • Table 2 describes examples and comparative examples in which the content (a) of Nb was changed when M was only Nb and Cu, X3, and B were not included.
  • Table 3 describes examples and comparative examples in which the Cu content (c) was changed when M was only Zr and X3 and B were not included.
  • Table 4 describes examples and comparative examples in which the type and content (d) of X3 are changed when M is only Zr and Cu and B are not included.
  • Table 5 describes examples and comparative examples in which the content (e) of B was changed when M was only Zr and Cu and X3 were not included.
  • Examples 24 to 27 in which the content of each component was within a predetermined range had good saturation magnetic flux density Bs, coercive force Hc, and specific resistance ⁇ .
  • Table 6 describes examples in which the type of M was changed from Example 3.
  • Examples 28 to 32 in which the content of each component is within a predetermined range even when the type of M is changed have good saturation magnetic flux density Bs, coercive force Hc, and specific resistance ⁇ .
  • Table 7 describes examples and comparative examples in which the content of Zr (a) and the content of Si (b) were changed when M was Zr only and Cu, X3 and B were not included. . As described above, with respect to the examples and comparative examples shown in Table 7, changes in saturation magnetic flux density and coercive force due to changes with time were measured.
  • Examples 32a to 32d and 52 to 56 were excellent in saturation magnetic flux density, coercive force, and specific resistance, and the change in saturation magnetic flux density and coercive force with time was small.
  • Comparative Example 8a having too little Si has a large coercive force, and also has a large change with time in the saturation magnetic flux density and the coercive force.
  • Comparative Example 11 with too much Si resulted in a large coercive force. Further, as compared with Examples 52 to 56 having the same Zr content, the saturation magnetic flux density was also reduced.
  • Table 8 describes an example in which part of Fe in Example 3 was replaced with X1 and / or X2.
  • Table 9 shows examples and comparative examples in which the average grain size of the initial microcrystals and the average grain size of the Fe-based nanocrystalline alloy were changed by changing the rotation speed of the roll, the heat treatment temperature and / or the heat treatment time for Example 3. Is described.

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Abstract

L'invention concerne un alliage magnétique doux qui présente une densité de flux magnétique saturée élevée, un faible champ coercitif et une résistance spécifique élevée, et qui présente une formule de composition telle que （Ｆｅ（１－（α＋β））Ｘ１αＸ２β）（１－（ａ＋ｂ＋ｃ＋ｄ＋ｅ））ＭａＳｉｂＣｕｃＸ３ｄＢｅ. X1 représente au moins un élément choisi dans un groupe constitué de Co et de Ni, X2 représente au moins un élément choisi dans un groupe constitué de Ｔｉ, Ｖ, Ｍｎ, Ａｇ，Ｚｎ, Ａｌ, Ｓｎ，Ａｓ, Ｓｂ, Ｂｉ et d'éléments terres rares, X3 représente au moins un élément choisi dans un groupe constitué de C et Ge, M représente au moins un élément choisi dans un groupe constitué de Ｚｒ, Ｎｂ, Ｈｆ, Ｔａ, Ｍｏ et Ｗ, ０,０３０≦ａ≦０,１２０, ０,０２０≦ｂ≦０,１７５, ０≦ｃ≦０,０２０, ０≦ｄ≦０,１００, ０≦ｅ≦０,０３０, α≧０, β≧０, et ０≦α＋β≦０,５５.
PCT/JP2019/005514 2018-02-21 2019-02-15 Alliage magnétique doux et composant magnétique Ceased WO2019163661A1 (fr)

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JP2016211067A (ja) * 2015-04-30 2016-12-15 メトグラス、インコーポレイテッド ナノ結晶合金の前駆体である広幅の鉄基非晶質合金
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